WO2024251962A1

WO2024251962A1 - A high strength q&p steel strip or sheet, and a method for producing the same

Info

Publication number: WO2024251962A1
Application number: PCT/EP2024/065763
Authority: WO
Inventors: Daniel Krizan; Johannes REHRL; Christoph KICKINGER
Original assignee: Voestalpine Stahl GmbH
Current assignee: Voestalpine Stahl GmbH
Priority date: 2023-06-09
Filing date: 2024-06-07
Publication date: 2024-12-12
Anticipated expiration: 2025-12-09
Also published as: SE2350707A1; SE547265C2

Abstract

The invention relates to a high strength steel strip or sheet having: a composition comprising of the following elements in wt. %: C 0.10 – 0.30, Mn 1.5 – 3.0, Si 0.5 – 2.0, Al 0.03 – 0.50, Ti 0.01 – 0.10, B 0.002 – 0.008, optionally Nb, V, Cr, Mo, balance Fe apart from impurities, mechanical properties TS 980 – 1300 MPa, and optionally one or more of: YS 600 – 1100 MPa, HER ≥ 20 %, and TE ≥ 13 %, and a microstructure e fulfilling in vol. %: Ferrite 5 – 50, tempered martensite 20 – 85, bainite 0 – 15. fresh martensite 0 – 10 and retained austenite 5 – 20. The invention also relates to a method for producing a high strength steel strip or sheet.

Description

A HIGH STRENGTH Q&P STEEL STRIP OR SHEET. AND A METHOD FOR PRODUCING

THE SAME

TECHNICAL FIELD

The present invention relates to high strength steel strip or sheets suitable for applications in automobiles. In particular, the invention relates to cold rolled steel strip or sheets which have been produced by a process comprising intercritical annealing followed quenching and partitioning.

BACKGROUND ART

For a great variety of applications increased strength levels are a pre-requisite for light-weight constructions in the automotive industry, since car body mass reduction results in reduced fuel consumption.

Automotive body parts are often stamped out of sheet steels, forming complex structural members of thin sheet. However, such parts cannot be produced from conventional high strength steels, because of a too low formability for complex structural parts. For this reason, multiphase Transformation Induced Plasticity aided steels (TRIP steels) have gained considerable interest in the last years, in particular for application in auto body structural parts.

TRIP steels possess a multi-phase microstructure, which includes a meta-stable retained austenite phase, which is capable of producing the TRIP effect. When the steel is deformed, the austenite transforms into martensite, which results in remarkable work hardening. This hardening effect acts to resist necking in the material and postpones failure in sheet forming operations. The microstructure of a TRIP steel can greatly alter its mechanical properties.

Quenching & Partitioning (Q&P) is an annealing cycle which consists of a quenching and a partitioning step. In the quenching step, fully austenitized or intercritically annealed steels are quenched to a temperature between the martensite start temperature Ms and the martensite finish temperature MF to reach a partial martensitic transformation. The quenched steels are then held at a temperature either at or above the initial quenching temperature. Austenite that prevails after quenching is stabilized through carbon partitioning from martensite into the austenite during the partitioning.

Liquid Metal Embrittlement(LME) is a phenomenon where certain metals like Al and steels undergo brittle failure when stressed in contact with liquid metals like Zn, Sn, Pb, etc. One of the challenges in the welding industry is cracking due to LME observed on spot welds of Zn-coated High Strength Steel. Liquid zinc penetration results in a drastic reduction in the strength and ductility of the steel. LME can occur when there is a contact between the solid material and the embrittling liquid metal. Under certain conditions, the contact between the alloy and the liquid metal may result in a rapid penetration of the liquid phase along grain boundaries. In the absence of external stress, the phenomenon is known as grain boundary penetration, and the associated thermodynamic driving force is the reduction of interfacial energy. Grain boundary penetration is observed if the condition YGB > 2ysL is satisfied, where YGB is the grain boundary energy and YSL is the solid-liquid interface energy. In fact, higher YGB results in an increased driving force for the penetration.

High strength Si grades have a strong propensity to LME. An index that has been used in the industry gives that the relation C + Si/4 < 0.4 should be satisfied to ensure low propensity to LME (C and Si in weight %).

EP 3 394 298 Bl discloses a process for the production of a high-strength steel sheet with intercritical single annealing and Q&P. The steel comprises 0.15 - 0.23 C, 2 - 2.8 Mn, 1.0 - 2.1 Si, 0.02 - 1.0 Al, 1.7 - 2.1 Si + Al, 0 - 0.035 Nb, 0 - 0.3 Mo, 0 - 0.4 Cr, balance Fe and impurities. B and Ti are not intentionally added, and B is therefore less than 0.0010 while Ti is limited to 0.05. The patent proposes two relations to reduce LME sensitivity: (1) C + Si/10 < 0.3% and (2) Al > 6*(C + Mn/10)- 2.5%.

EP 3 656 880 Bl discloses a process for the production of a high-strength steel sheet with intercritical single annealing and Q&P. The steel comprises 0.15 - 0.23 C, 1.4 - 2.6 Mn, 0.6 - 1.5 Si, 0.02 - 1.0 Al, 1.0 - 2.0 Si+ Al, 0 - 0.035 Nb, 0 - 0.3 Mo, 0 - 0.3 Cr, balance Fe and impurities. B and Ti are not intentionally added, and B is therefore less than 0.0010 while Ti is limited to 0.05. The patent proposes two relations to reduce LME sensitivity: (1) C + Si/10 < 0.3% and (2) Al > 6*(C + Mn/10)- 2.5%.

EP 2 604 715 Bl discloses a process for the production of high-strength cold-rolled steel sheet. The steel sheet including 0.05 - 0.3 C, 0.3 - 2.5 Si, 0.5 - 3.5 Mn, 0.003 - 0.100 P, < 0.02 S, 0.010 - 0.5 Al, optionally at least one element selected from Cr: 0.005 to 2.00, Mo: 0.005 to 2.00, V: 0.005 to 2.00, Ni: 0.005 to 2.00, and Cu: 0.005 to 2.00, optionally one or both ofTi: 0.01 to 0.20 and Nb: 0.01 to 0.20, optionally B: 0.0002 to 0.005, optionally one or both of Ca: 0.001 to 0.005 and REM: 0.001 to 0.005, and balance being iron and unavoidable impurities. The process comprises intercritical single annealing with Quenching & Partitioning, in which the average heating rate from 500°C to Ael transformation point should be 10°C/s or more to supress recrystallization during heating. This is to achieve a fine grain structure, which improves the crashworthiness. Not all facilities are capable of such high heating rates to the annealing and the high heating rates may also add extra costs. EP 3 859 041 Al discloses a High-strength cold-rolled steel sheet with Q&P cycle, full austenitic annealing followed by quenching and tempering. It suggests that if silicon exceeds 0.8 %, deterioration of physical properties of a weld portion due to formation of LME cracks cannot be prevented and surface characteristics and plating properties of the steel deteriorate. The document proposes an equation which should be fulfilled to avoid that LME resistance is deteriorated during spot welding: C + (Si + Al)/5 < 0.35%.

It would be advantageous to improve LME resistance without restrictions on C, Si, and Al. Furthermore, it would be advantageous if production costs can be kept low, and that it is possible to produce the steel sheets in a wide variety of continuous annealing lines.

DISCLOSURE OF THE INVENTION

The present invention is directed to steel strip or sheets having a tensile strength of 980 - 1300 MPa. The steel strip or sheets are produced in a single annealing process of which the annealing cycle includes intercritical annealing, quenching to a temperature between Ms-20 °C and MF and partitioning at a temperature above the quenching temperature. By adding Ti+B to the composition, it is possible to be free of cracks longer than 300 pm in the heat affected zone of spot weld joints. The addition of B is believed to reduce the austenite/austenite interface energy such that YGB < 2ysL. Ti binds N so that B remains free to protect the austenitic grain boundaries. Ti and B are increased by a factor of 10 compared to normal impurity levels.

BRIEF DECRIPTION OF THE DRAWING

Fig. 1 shows schematically the annealing cycle of the invention.

DETAILED DESCRIPTION

In a preferred embodiment the strip or sheet has a composition consisting of the following alloying elements (in wt. %):

C 0.10 - 0.30

Mn 1.5 - 3.0

Si 0.5 - 2.0

Al 0.03 - 0.50

Ti 0.01 - 0.10

B 0.002 - 0.008

Optionally

Nb < 0.1 V < 0.1

Cr < 0.8

Mo < 0.2 balance Fe apart from impurities.

The composition is excluding any coatings applied to the strip or sheet.

The importance of the separate elements and their interaction with each other as well as the limitations of the chemical ingredients of the claimed alloy are briefly explained in the following. All percentages for the chemical composition of the steel are given in weight % (wt. %) throughout the description. Upper and lower limits of the individual elements can be freely combined within the limits set out in the claims. The arithmetic precision of the numerical values can be increased by one or two digits for all values given in the present application. Hence, a value of given as e.g. 0.1 % can also be expressed as 0.10 or 0.100 %. The amounts of the microstructural constituents are given in volume % (vol. %).

C: 0.10 - 0.30 %

C stabilizes the austenite and is important for obtaining sufficient carbon within the retained austenite phase. C is also important for obtaining the desired strength level. Generally, an increase of the tensile strength in the order of 100 MPa per 0.1 % C can be expected. When C is too low it is difficult to attain a sufficient tensile strength. If C is too large the weldability is impaired. The upper limit is therefore 0.30 % and may be restricted to 0.29, 0.28, 0.27, 0.26, 0.25, 0.24, 0.23 or 0.22 %. The lower limit may be 0.10, 0.12, 0.14, or 0.16 %.

A preferred range is 0. 16 - 0.22 %.

Si: 0.5 - 2.0 %

Si acts as a solid solution strengthening element and is important for securing the strength of the thin steel strip. Si suppresses the cementite precipitation and is essential for austenite stabilization.

However, if the content is too high, then too much silicon oxides will form on the strip surface, which may lead to cladding on the rolls in the CAL and, as a result thereof, to surface defects on subsequently produced steel sheets. The upper limit is therefore 2.0 % and may be restricted to 1.9, 1.8, 1.7 or 1.6 %. The lower limit may be 0.5, 0.6, 0.7, or 0.8 %.

A preferred range is 0.8 - 1.6 %.

Mn: 1.5 - 3.0 %

Manganese is a solid solution strengthening element, which stabilises the austenite by lowering the M_s temperature and prevents ferrite and pearlite to be formed during cooling. In addition, Mn lowers the Ae3 temperature and is important for the austenite stability. At too low contents it might be difficult to obtain the desired amount of retained austenite, a sufficient tensile strength, and the austenitizing temperature might be too high for conventional industrial annealing lines. In addition, at lower contents it may be difficult to avoid the formation of polygonal ferrite. However, if the amount of Mn is too high problems with segregation may occur because Mn accumulates in the liquid phase and causes banding, resulting in a potentially deteriorated workability. The upper limit may therefore be 3.0, 2.9, 2.8, 2.7 or 2.6 %. The lower limit may be 1.5, 1.6, 1.7, 1.8, 1.9, 2.0 or 2.1%.

A preferred range is 2. 1 - 2.6 %.

Al: 0.03 - 0.50 %

Additions of Al can increase the carbon content in the retained austenite. Al can also be used as a deoxidizer. Al, like Si, is not soluble in the cementite can therefore delay cementite formation during bainite formation and martensite tempering. An addition of Al can further improve galvanization and reduce the susceptibility to LME. The Ms temperature is also increased with increasing Al content. A drawback of Al is that it results in an increase of the Ae3 temperature. The upper limit may be 0.5, 0.4, 0.3, 0.2, 0.1%. The lower limit may be set to 0.03, 0.04, 0.05, 0.06, 0.07, 0.08, 0.09, or 0. 1 %.

If Al is used for deoxidation only, the upper limit may be 0.10, 0.09, 0.08, 0.07 or 0.06 %. For securing a certain effect the lower level may set to 0.03 or 0.04 %.

A preferred range is 0.03 - 0. 1 %.

B: 0.002 - 0.008 %

The steel is alloyed with B to reduce the austenite/austenite interface energy (YGB) to prevent grain boundary penetration, i.e. YGB < 2 YSL B suppresses the formation of ferrite and improves the weldability of the steel sheet. However, excessive amounts of B deteriorate the workability. The upper limit may be set to 0,08, 0.07, 0.06, 0.05, or 0.004 %. The lower limit may be set to 0.002 or 0.0025 %. A preferred range is 0.0025 - 0.004 %.

Ti: 0.01 - 0.10 %

Ti improves strength and toughness, because of its influence on the grain size by forming carbides, nitrides or carbonitrides. In this steel, Ti is primarily added to bind the nitrogen in the steel so that B remains free to protect the austenitic grain boundaries. The effect of Ti is saturated above 0.1 %. The upper limit may be set to 0.10, 0.09, 0,08, 0.07, 0.06, or 0.05 %. The lower limit may be set to 0.01, 0.015, 0.02, 0.03, 0.04, or 0.05 %. A preferred range is 0.015-0.050 %.

Optional limitations

The microalloying with Ti and B improves the weldability by reducing the LME sensitivity. This makes it possible to avoid LME cracks even when one or more of the following conditions are not met:

(1) C + Si/10 < 0.3%

(2) Al > 6*(C + Mn/10) - 2.5%

(3) C + (Si + Al)/5 < 0.35%.

Therefore a LME resistant steel can be produced where C + Si/10 > 0.3% and/or Al < *(C + Mn/10)- 2.5% and/or C + (Si + Al)/5 > 0.35%. The content in weight % of each element.

Optional elements

Nb: < 0.1 %

Nb is commonly used in low alloyed steels for improving strength and toughness, because of its influence on the grain size. Nb increases the strength elongation balance by refining the matrix microstructure and the retained austenite phase due to precipitation of NbC. The steel may contain Nb in an amount of < 0.1%. The upper limit may be restricted to 0.09, 0.07, 0.05, 0.03, 0.01, or 0.005 %. A lower limit may be 0.001, 0.01, or 0.05 %. A deliberate addition of Nb is not necessary according to the present invention.

V: < 0.1 %

The function of V is similar to that of Nb in that it contributes to precipitation hardening and grain refinement. The steel may contain V in an amount of < 0. 1 %. The upper limit may be restricted to 0.09, 0.07, 0.05, 0.03, or 0.01 %. A lower limit may be 0.001, 0.01, or 0.05 % A deliberate addition of V is not necessary according to the present invention.

Cr: < 0.8 %

Cr is effective in increasing the strength of the steel sheet. Cr is an element that forms ferrite and retards the formation of pearlite and bainite. The Ae3 temperature and the M_s temperature are only slightly lowered with increasing Cr content. Cr results in an increased amount of stabilized retained austenite. Too much Cr may impair the surface finish of the steel. The amount of Cr is is limited to 0.8 %. The upper limit may be 0.7, 0.6, 0.5, 0.4, 0.3, 0.2, 0.1 or 0.05 %. The lower limit may be 0.01, 0.03, 0.05, 0.07, 0.10, 0.15, 0,20 or 0.25 %. Preferably, a deliberate addition of Cr is not conducted according to the present invention.

Mo < 0.2 %

Molybdenum is a powerful hardenability agent. It may further enhance the benefits of NbC precipitates by reducing the carbide coarsening kinetics. The steel may therefore contain Mo in an amount up to 0.2 %. Mo delays the decomposition of austenite and stabilizes the retained austenite. Amounts of more than 0.2 % result in high costs. The upper limit may be restricted to 0.2, 0.1, 0.05, 0.01 %. The lowest amount may be set to 0.001, 0.005, 0.01, 0.02, 0.03, 0.04 or 0.05 %. A deliberate addition of Mo is not necessary according to the present invention.

Impurities

The following impurities may optionally be limited as disclosed below.

Ca: < 0.05 %

Ca could be used for the modification of the non-metallic inclusions. The upper limit is 0.05% and may be set to 0.04, 0.03, 0.01, or 0.005 %. A deliberate addition of Ca is not necessary according to the present invention.

Cu: < 0.1 %

Cu is an undesired impurity element that is restricted to < 0. 1 % by careful selection of the scrap used. The upper limit is 0.1% and may be further restricted to 0.05 %.

Ni: < 0.2 %

Ni is also an undesired impurity element that is restricted to < 0.2 % by careful selection of the scrap used. The upper limit is 0.2% and may be further restricted to 0.1 or 0.05 %.

Other impurity elements may be comprised in the steel in normal occurring amounts. However, it is preferred to limit the amounts of P, S, As, Zr, Sn to the following optional maximum contents:

P: < 0.05, < 0.04, < 0.03 or < 0.02 %

S: < 0.05, < 0.03, < 0.01, <0.005 or < 0.001 %

As: < 0.020, or < 0.010 %

Zr: < 0.010, or < 0.006 %

Sn: < 0.030, or < 0.015 %

Oxygen and hydrogen can further be limited to

O: < 0.001, or < 0.0003 %

H: < 0.0050, or < 0.0020 %

It is also preferred to control the nitrogen content to the range:

N: < 0.015 %, preferably 0.001 - 0.008 %

Mechanical properties

The steel should fulfil the following condition on the tensile strength:

TS, Tensile Strength (Rm) 980 - 1300 MPa And optionally one or more of the following mechanical properties:

YS, Yield Strength (R_p02) 600 - 1100 MPa

HER, Hole Expansion

Ratio ( ) > 20 %

TE, Total

Elongation (Ago) > 13 %

Preferably, all these requirements are fulfilled at the same time.

Different strength grades may be produced having the following mechanical properties:

Steel grades 980 1180

TS, Tensile Strength (Rm) 980 - 1100 MPa 1180 - 1300 MPa

YS, Yield Strength (Rpo.2) 600 - 850 MPa 850 - 1100 MPa HER, Hole Expansion Ratio ( ) > 20 % > 30 % TE, Total Elongation (Ago) > 18 % > 13%

The strip or sheet thickness of the final product may be 0. 1 - 4 mm, preferably 0.5 - 3 mm. The strip or sheet width may be 500 - 2000 mm, preferably 700 - 1750 mm in non-slit condition.

Preferably, the sheet or strip is provided with at least one spot welded joint, each having a heat affected zone around it, wherein the heat affected zone/s are free of cracks longer than 300 pm.

Microstructure

The microstructural constituents are in the following expressed in volume % (vol. %).

Ferrite 5 - 50 tempered martensite 20 - 85 bainite 0 - 15 fre sh martensite 0 -10 retained austenite (RA) 5 - 20

Each of the phases in the list above may balance the microstructure.

Preferably, the average grain diameter is in the range of 3 -30 pm, more preferably 5 - 25 pm, most preferably 5 - 25 pm. The average grain size can be determined using the intercept procedure described in ASTM El 12-13(2021) “Standard Test Methods for Determining Average Grain Size”. Ferrite is the sum of intercritical and proeutectoid ferrite and should be between 5 - 50 vol. %. The lower limit may be 5, 10, 15, or 20 vol. %. The upper limit may be 50, 40 or 30 vol %. A preferred range for grade 980 is 20-40 vol. % and for grade 1180 a preferred range is 10 - 30 vol. %.

Tempered martensite is martensite from the quenching step that is tempered in the partitioning step. The lower limit of tempered martensite may be 20, 25, 30, 35, or 40 vol. %. The upper limit may be 85, 70, 60, or 50 vol %. A preferred range is 30 - 70 vol. %. A more preferred range for grade 980 is 30-60 vol. %, and for grade 1180 a more preferred range is 40 - 70 vol. %.

The steel may contain bainite. The upper limit of bainite may be 15, 10, 5, or 0 vol %. The lower limit may be 0, 5, or 10 vol %. A preferred range for grade 980 is 5 - 10 vol. % and for grade 1180 a preferred range is 0 - 10 vol. %.

Fresh martensite can be formed upon final cooling after quenching and partitioning. The upper limit of fresh martensite may be 10 or 5 vol.%. A preferred range is 0 - 5 vol. %.

Retained austenite is a prerequisite for obtaining the desired TRIP effect. The amount of retained austenite should be in the range of 5 - 20 vol %, preferably 10 - 20 vol %.

The steel grades 980 and 1180 may be limited to the following microstructures which includes rpefred ranges for each phase.

Steel grades 980 1180

Ferrite (vol. %) 20 - 40 10 - 30

Tempered Martensite (vol. %) 30 - 60 40 - 70

Bainite (vol. %) 5 -10 0 - 10

RA (vol. %) 10 - 20 10 - 20

Fresh Martensite (vol. %) 0 - 5 0 - 5

Definitions

Temperatures are given in degrees Celsius throughout the description.

Ae 1 refers to the temperature at which austenite begins to form in a steel and Ae3 temperature is the temperature at which the steel becomes fully austenitic. Ael and Ae3 are calculated by means of ThermoCalc 2022 TCFE 12. Ms temperature is calculated using the Ms formula found in S. Kaar, K. Steineder, R. Schneider, D. Krizan and C. Sommitsch: „New Ms-formula for exact microstructural prediction of modem 3rd generation AHSS chemistries”, Scr. Mater., Vol. 200, 2021, 113923.

Ms = 692 - 502 * (C + 0.86 * N) ^A 0.5 - 37 * Mn - 14 * Si + 20 * Al - 11 * Cr

The Ms formula uses the content in weight % of each element.

MF formula is derived from Koistinen-Marburger equation found in (Koistinen, D. and Marburger, R: “A general equation prescribing the extent of the austenite-martensite transformation in pure ironcarbon alloys and plain carbon steels”, Acta Metall, 7, 1959, pp. 59 - 60):

M_F = M_s + [ln(l- f_M)]/0.011, where the fraction of martensite fM is 0.95.

The microstructure, including the amount of each phase, can be identified in scanning electron microscope (SEM) using 2000 times magnification. Preferably by cutting out a sample from a steel plate and polishing a cross section of a plate parallel to the rolling direction. The microstructure should be taken from ! of the thickness. The surface can be etched to make the phases easier to identify.

However, the amount of retained austenite is preferably determined by means of the saturation magnetization method described in detail in Proc. Int. Conf, on TRIP-aided high strength ferrous alloys (2002), Ghent, Belgium, p. 61 - 64.

The Rm, Rpo 2 values as well as the total and/or uniform elongation are derived in accordance with the Industrial Standard DIN EN ISO 6892-1, wherein the samples with a gauge length of 80 mm are taken in the longitudinal direction of the strip.

The hole expansion ratio ( ) is determined by the hole expansion test according to ISO/WD 16630:2009 (E). In this test a conical punch having an apex of 60° is forced into a 10 mm diameter punched hole made in a steel sheet having the size of 100 x 100 mm². The test is stopped as soon as the first crack is determined, and the hole diameter is measured in two directions orthogonal to each other. The arithmetic mean value is used for the calculation.

The hole expanding ratio (X) in % is calculated as follows:

X = (Dh - Do)/Do X 100 wherein Do is the diameter of the hole at the beginning (10 mm) and Dh is the diameter of the hole after the test.

LME Crack length can be determined by the following method. First a maximum current Imaxis determined in accordance with the standardized test described in SEP1220-2 (Stahl Eisen Priifblatter) - for the standard two sheet combination. In a second step a three -sheet combination subjected to RSW (resistant spot welded joint) at the same current (I_max) but at a welding time five times longer in order to increase the heat input. For each combination 8 spots are welded and the occurrence of the cracks in the Heat Affected Zone (HAZ) are manually examined in a light optical microscope on metallographically prepared samples.

The formula YGB > 2ysL is described in the publications Journal of Materials Science 14 (1979) 1-18; “Review Liquid metal embrittlement”, and Progress in Materials Science 121 (2021) 100798; “Pathway to understand liquid metal embrittlement (LME) in Fe-Zn couple: From fundamentals toward application”. These are incorporated by reference.

Unless otherwise specified, parameter values throughout the description including the Examples are determined by the methods given in this section.

Production of a cold rolled strip.

A cold rolled steel strip may be produced by the following steps: a) Making steel slabs with the composition defined above. The steel slabs may e.g. be produced by converter melting or in an electric steel plant and secondary metallurgy to finalise the composition b) The slabs are hot rolled in austenitic range to a hot rolled strip. Preferably by reheating the slab to a temperature between 1000 °C and 1280 °C. Preferably rolling the slab completely in the austenitic range wherein the hot rolling finishing temperature is greater than or equal to 850 °C to obtain the hot rolled steel strip. c) Thereafter, the hot rolled strip may be coiled at a coiling temperature in the range of 400 - 700 °C. d) Optionally subjecting the coiled strip to a scale removal process, such as pickling. e) Optionally annealing at a temperature in the range of 450 - 950 °C. Preferably batch annealing at 450 - 650 °C, for a duration of 2 - 30 h, more preferably 5 - 20 h. The strip may alternatively be continuously annealed at temperature in the range of 650 - 950 °C for 10 - 200 s. f) Optionally subjecting the annealed strip to a scale removal process, such as pickling. g) Thereafter cold rolling the annealed steel strip at a reduction rate between 20 - 90 %, preferably around 50 - 70 % reduction. The steps a) - g) of producing the cold rolled strip described above are examples on how the cold rolled strip can be produced. The invention may also be applied to cold rolled strips that are produced under similar but different processing conditions as known in the art.

Intercritical annealing with Quenching and Partitioning h) Providing a cold rolled steel strip to a continuous annealing line, the steel strip having a composition as suggested above. i) heating the strip to an annealing temperature (Tan) between Ae 1 and Ae3, preferably between Ael + 20 °C and Ae3 - 20 °C. In the range of 500 °C to the annealing temperature (Tan), the heating rate (HR1) is < 10 °C/s, preferably < 5 °C/s. j) soaking for 10 - 300 s (tan) at the annealing temperature (Tan). The annealing temperature (Tan) and soaking time are controlled to reach a desired amount of intercritical ferrite and austenite. k) cooling the strip at a rate (CR1) of 5 - 100 °C/s, preferably 10 - 50 °C/s, to a first quenching temperature (Tq) between MF and (Ms - 20) °C. The lower limit may further be restricted to the highest of MF and value chosen from 150, 160, 170, and 180 °C. The upper limit may further be restricted to Ms - 30, Ms - 40, Ms - 50, Ms - 60, Ms - 70, Ms - 80, Ms - 90, or Ms - 100 °C. The cooling rate (CR1) may further be restricted to < 20 °C/s. l) heating the cooled strip at a rate (HR2) of 10 - 100 °C/s, preferably 20 - 50 °C/s, to a first partitioning temperature (Tp) in the range of the first quenching temperature (Tq) + 10 °C to 500 °C and partitioning the strip for 20 - 1000 s (tp). Preferably the first partitioning temperature (Tq) is above Ms. The upper limit may be restricted to 500, 480, 450, 430, or 410 °C. The lower limit may be restricted to 260, 280, 300, 320, 340, 360, or 380 °C. m) cooling the strip to a temperature below 50 °C, preferably to room temperature, at a rate (CR2) of 1 - 50 °C/s. n) optionally applying a coating though galvanising, galvannealing, electro galvanising, or physical vapor deposition. o) resistance spot welding of sheets from the strip.

Optional coating

The steel sheet or strip may optionally be coated and comprise a zinc or a zinc -alloy coating. The coating can e,g. be applied by:

Electrogalvanizing (EG) including electroplating.

Physical Vapor Deposition (PVD).

Hot Dip Galvanizing (HDG) in a Hot Dip Galvanizing Line, in which the strip is immersed in a molten zinc bath at the end of the final partitioning (step n). A Hot Dip Galvanizing Line can be the same line as a Continuous Annealing Line with added hot dip coating. Galvannealing (GA) in a Galvannealing line, which is the similar as the Hot Dip Galvanizing Line with the addition of an annealing step following the hot dip coating. I.e. processed the same way as the Continuous Annealing Line, but including galvannealing at the end of the final partitioning (step n). Galvannealing is a combination of galvanizing and annealing around 480 - 560°C in order to facilitate a higher degree of Fe in the ZnFe coating.

A zinc alloy coating may comprise in weight %:

Mg 0.1 - 10

Al 0.1 - 10 Optionally one or more of:

Bi, Pb, Sn, Sb, Si, Ti, Ca, Mn, La, Ce, Cr, Ni and Zr in a total amount of 0.01 - 1.0 Balance Zn and impurities.

A galvannealed coating may contain 5 - 20 wt.% of diffused Fe.

Other coating composition known in the art can be applied.

EXAMPLES

Ten alloys LI - LIO were produced by conventional metallurgy by converter melting and secondary metallurgy. The compositions of the alloys (elements are in [wt%]) are shown in table 1, further elements were present only as impurities, and below the lowest levels specified in the present description. LI - L3, and L8 are reference grades with low Ti and B. The inventive samples L4 - L7 and L9 - LIO all had a substantial addition of Ti and B.

Table 1

The alloys LI - LIO were continuously cast and cut into slabs. The slabs were reheated and hot rolled in austenitic range to a thickness of about 2.8 mm. The hot rolling finishing temperature was about

900 °C. The hot rolled steel strips where thereafter coiled at a coiling temperature of 550 °C. The coiled hot rolled strips were pickled and batch annealed at about 560 °C for 10 hours in order to reduce the tensile strength of the hot rolled strip and thereby reducing the cold rolling forces. The strips were thereafter cold rolled in a five-stand cold rolling mill to a final thickness of about 1.4 mm. The steels were subjected to Intercritical annealing with Quenching and Partitioning in a continuous annealing line. The process values are shown in Table 2 and the annealing cycle is schematically shown in Pig. 1. Table 2

Different properties were determined, and the results are shown in Table 3. The mechanical properties - Yield strength, Tensile strength, Uniform Elongation, Total Elongation, Hole Expansion Ratio are similar for the reference grades LI - L3; L8 compared to the inventive grades L4 - L7; L9 - LIO.

Also, the amounts of each phase of the microstructures were similar. The retained austenite is shown in the table 3. The other microstructural phases were checked that they were within the defined boundaries of respective steel grade 980, 1180. The average grain diameter of the microstructure was around 15 pm for each steel grade 980, 1180.

Table 3

The LME Crack length was determined in a two step test. First, the maximum current I_max was determined in accordance with the standardized test described in SEP1220-2 (Stahl Eisen Priifblatter) for the standard two sheet combination. In the second step a three-sheet combination was subjected to

RSW (resistant spot welded joint) at the same current (Imax) but the welding time was five times in order to increase the heat input. For each combination 8 spots were welded and the occurrence of cracks in the Heat Affected Zone (HAZ) was manually examined in a light optical microscope on metallographically prepared samples. Remarkable differences in the LME Crack length were observed. It was found that there was not any HAZ cracks longer than 300 pm in any of the samples L4 - L7 and L9 - LIO (in the inventive samples) The 1180 grades had a reduction from 1360.7pm (±174.5pm) of the reference alloys LI - L3 to 201.5pm (±14.2pm) of the inventive alloys L4 - L7. The 980 grades had a reduction from 914 pm of the reference alloy L8 to 182.5pm (±2.5pm) of the inventive alloys L9 - L10.

Hence, by adding Ti±B to the alloy and subjecting it to an intercritical annealing cycle with Q&P process, it is possible to be free of cracks longer than 300 pm in the heat affected zone of spot weld joints.

Claims

1. A high strength steel strip or sheet having: i) a composition consisting of the following elements in wt. %:

C 0.10-0.30

Mn 1.5 -3.0

Si 0.5 -2.0

Al 0.03-0.50

Ti 0.01-0.10

B 0.002-0.008

Optionally

Nb <0.1

V <0.1

Cr <0.8

Mo <0.2 balance Fe apart from impurities; ii) TS, Tensile Strength (Rm) 980 - 1300 MPa and optionally at least one of: YS, Yield Strength (Rpo 2) 600- 1100 MPa HER, Hole Expansion Ratio (A)

TE, Total Elongation (Ago)

wherein the Rm. Rpo 2 values as well as the total elongation are derived in accordance with the Industrial Standard DIN EN ISO 6892-1 including samples with a gauge length of 80 mm are taken in the longitudinal direction of the strip, and the hole expansion ratio (X) is determined by the hole expansion test according to ISO/WD 16630:2009 (E). in) microstructure fulfilling the following requirements in vol. %: Ferrite 5-50 tempered martensite 20-85 bainite 0- 15 fresh martensite 0- 10 retained austenite 5-20

2. The steel strip or sheet according to claim 1. comprising at least one spot welded joint, each having a heat affected zone around it. wherein the heat affected zone/s are free of cracks longer than 300 pm.

3. The steel strip or sheet according to claim 1 or 2. wherein the microstructure fulfils at least one of the following requirements in vol. %. preferably all the requirements:

Ferrite 20 - 40 tempered martensite 30 - 60 bainite 5 - 10 fresh martensite 0 - 5 retained austenite 10 - 20

4. The steel strip or sheet according to claim 3. wherein one or more of the following mechanical properties are fulfilled:

TS, Tensile Strength (Rm) 980 - 1100 MPa YS, Yield Strength (Rpo 2) 600 - 850 MPa HER, Hole Expansion Ratio (A) > 20 %

TE, Total Elongation (Ago) > 18 %

5. The steel strip or sheet according to claim 1 or 2. wherein the microstructure fulfils at least one of the following requirements in vol. %. preferably all the requirements:

Ferrite 10 - 30 tempered martensite 40 - 70 bainite 0 - 10 fresh martensite 0 - 5 retained austenite 10 - 20

6. The steel strip or sheet according to claim 5. wherein one or more of the following mechanical properties are fulfilled:

TS, Tensile Strength (Rm) 1180 - 1300 MPa YS, Yield Strength (Rpo 2) 850 - 1100 MPa HER. Hole Expansion Ratio (A) > 30 %

TE, Total Elongation (Ago) > 13 %

7. The high strength steel strip or sheet according to any one of the preceding claims having a composition consisting of the following alloying elements (in wt. %):

C 0.16 - 0.22

Si 0.8 - 1.6

Mn 2.1 - 2.6

Al 0.03 -0.1

Ti 0.015 - 0.050

B 0.0025 - 0.004

Optionally

Nb < 0.1

V < 0.1

Cr < 0.8

Mo < 0.2 balance Fe apart from impurities.

8. The high strength steel strip or sheet according to any one of the preceding claims comprising a zinc alloy coating.

9. The high strength steel strip or sheet according to claim 8 wherein the zinc alloy coating comprises in weight %:

Mg 0.1 - 10

Al 0.1 - 10

Optionally one or more of: Bi, Pb, Sn, Sb, Si, Ti, Ca, Mn, La, Ce, Cr, Ni and Zr in a total amount of 0.01 - 1.0

Balance Zn and impurities.

10. A method for producing a high strength steel strip or sheet according to any one of claims 1 - 9. comprising: h) providing a cold rolled steel strip having a composition as defined in any one of claims 1-9, i) heating the strip to an annealing temperature (Tan) between Ae 1 and Ae3. wherein in the range of 500 °C to the annealing temperature (Tan), the heating rate (HR1) is < 10 °C/s. j) soaking for 10 - 300 s (tan) at the annealing temperature (Tan), k) cooling the strip at a rate (CR1) of 10 - 100 °C/s to a quenching temperature (Tq) between MF and (Ms-20) °C, l) heating the cooled strip at a rate (HR2) of 10 - 100 °C/s to a partitioning temperature (Tp) in the range of the quenching temperature (Tq) + 10 °C to 500 °C. and partitioning the strip for 20 - 1000 s (tp), m) cooling the strip to a temperature below 50 °C at a rate (CR2) of 1 - 50 °C/s, n) optionally applying a coating though galvanising, galvannealing, electro galvanising, or physical vapor deposition, and o) resistance spot welding of sheets cut from the strip.

11. The method according to claim 10, wherein the cold rolled steel strip is produced by the following steps: a) making steel slabs with a composition as defined in any one of claim 1-9, b) hot rolling in austenitic range to a hot rolled strip, c) coiling the hot rolled strip at a coiling temperature in the range of 400 - 700 °C, d) optionally subjecting the coiled strip to a scale removal process, such as pickling, e) optionally annealing at a temperature in the range of 450 - 950 °C, f) optionally subjecting the annealed strip to a scale removal process, such as pickling, g) cold rolling the strip at a reduction rate between 20 - 90 %.